Fabrication of a semiconductor nanoparticle embedded insulating film electroluminescence device

ABSTRACT

A method is provided for fabricating a semiconductor nanoparticle embedded Si insulating film for electroluminescence (EL) applications. The method provides a bottom electrode, and deposits a semiconductor nanoparticle embedded Si insulating film, including an element selected from a group consisting of N and C, overlying the bottom electrode. After annealing, a semiconductor nanoparticle embedded Si insulating film is formed having an extinction coefficient (k) in a range of 0.01-1.0, as measured at about 632 nanometers (nm), and a current density (J) of greater than 1 Ampere per square centimeter (A/cm 2 ) at an applied electric field lower than 3 MV/cm. In another aspect, the annealed semiconductor nanoparticle embedded Si insulating film has an index of refraction (n) in a range of 1.8-3.0, as measured at 632 nm, with a current density of greater than 1 A/cm 2  at an applied electric field lower than 3 MV/cm.

RELATED APPLICATIONS

This application is a Continuation-in-part of a pending patent application entitled, LIGHT EMITTING DEVICE WITH A NANOCRYSTALLINE SILICON EMBEDDED INSULATOR FILM, invented by Huang et al., Ser. No. 12/126,430, filed May 23, 2008, which is a Continuation-in-Part of:

a patent application entitled, SILICON OXIDE THIN-FILMS WITH EMBEDDED NANOCRYSTALLINE SILICON, invented by Pooran Joshi et al., Ser. No. 11/418,273, filed May 4, 2006 now U.S. Pat No. 7,544,625, which is a Continuation-in-Part of the following applications:

ENHANCED THIN-FILM OXIDATION PROCESS, invented by Pooran Joshi et al., Ser. No. 11/327,612, filed Jan. 6, 2006 now U.S. Pat. No. 7,723,242;

HIGH-DENSITY PLASMA HYDROGENATION, invented by Pooran Joshi et al., Ser. No. 11/013,605, filed Dec. 15, 2004 now U.S. Pat. No. 7,446,023;

DEPOSITION OXIDE WITH IMPROVED OXYGEN BONDING, invented by Pooran Joshi, Ser. No. 10/801,377, filed Mar. 15, 2004 now U.S. Pat. No. 7,122,487;

HIGH-DENSITY PLASMA OXIDATION FOR ENHANCED GATE OXIDE PERFORMANCE, invented by Joshi et al., Ser. No. 11/139,726, filed May 26, 2005 now U.S. Pat. No. 7,381,595;

HIGH-DENSITY PLASMA PROCESS FOR SILICON THIN-FILMS, invented by Pooran Joshi, Ser. No. 10/871,939, filed Jun. 17, 2004 now U.S. Pat No. 7,186,663;

METHOD FOR FABRICATING OXIDE THIN-FILMS, invented by Joshi et al., Ser. No. 10/801,374, filed Mar. 15, 2004 now U.S. Pat. No. 7,087,537.

All the above-referenced applications are incorporated herein by reference.

BACKGROUND OF THE INVENTION

1. Field of the Invention

This invention generally relates to the fabrication of integrated circuit (IC) electroluminescence (EL) devices, and more particularly, to an EL device made from a semiconductor nanoparticle embedded insulating film, with controlled extinction coefficient (k) and electrical conductivity properties.

2. Description of the Related Art

The fabrication of integrated optical devices involves the deposition of materials with suitable optical characteristics such as absorption, transmission, and spectral response. Thin-film fabrication techniques can produce diverse optical thin films, which are suitable for the production of large area devices at high throughput and yield. Some optical parameters of importance include refractive index (n) and the optical band-gap, which dictate the transmission and reflection characteristics of the thin film.

Typically, bilayer or multilayer stack thin-films are required for the fabrication of optical devices with the desired optical effect. Various combinations of the metal, dielectric, and/or semiconductor layers are also used to form multilayer films with the desired optical characteristics. The selection of the material depends on the target reflection, transmission, and absorption characteristics. While a single layer device would obviously be more desirable, no single thin-film material has been able to provide the wide range of optical dispersion characteristics required to get the desired optical absorption, band-gap, refractive index, reflection, or transmission over a wide optical range extending from ultraviolet (UV) to far infrared (IR) frequencies.

Silicon is the material of choice for the fabrication of optoelectronic devices because of well-developed processing technology. However, the indirect band-gap makes it an inefficient material for optoelectronic devices. Over the years, various R&D efforts have focused on tailoring the optical function of Si to realize Si-based optoelectronics. The achievement of efficient room temperature light emission from the crystalline silicon is a major step towards the achievement of fully Si-based optoelectronics.

At present, the Si thin film-based photodetectors operating at wavelengths shorter than 850 nm are attractive for low cost, highly integrated CMOS devices. Si is an indirect bandgap semiconductor with limited speed-responsivity performance, but it is still useful for detection in UV-VIS (visible)-NIR (near-IR) spectrum. However, the indirect bandgap of Si limits the critical wavelength of Si to 1.12 μm, beyond which its absorption goes to zero, making it insensitive to two primary telecommunication wavelengths of 1.30 and 1.55 μm. An additional issue with Si based photo-detectors is the dark current limiting the signal-to-noise ratio (SNR), and the thermal instability at operating temperatures higher than 50° C.

The fabrication of stable and reliable optoelectronic devices requires Si nanocrystals with high photoluminescence (PL) and electroluminescence (EL) quantum efficiency. EL is both an optical phenomenon and an electrical phenomenon in which a material emits light in response to an electric current passed through it, or in response to a strong electric field. EL can be distinguished from light emission resulting from heat (incandescence) from the action of chemicals (chemoluminescence), the action of sound (sonoluminescence), or other mechanical action (mechanoluminescence). PL is a process in which a substance absorbs photons (electromagnetic radiation) and then re-radiates photons. Quantum mechanically, PL can be described as an excitation to a higher energy state and then a return to a lower energy state accompanied by the emission of a photon. The period between absorption and emission is typically extremely short, in the order of 10 nanoseconds.

One approach that is being actively pursued for integrated optoelectronic devices is the fabrication of SiO_(x) (x≦2) thin films with embedded Si nanocrystals. The luminescence due to recombination of the electron-hole pairs confined in Si nanocrystals depends strongly on the nanocrystal size. The electrical and optical properties of the nanocrystalline Si embedded SiO_(x)N_(y) thin films depend on the size, concentration, and distribution of the Si nanocrystals. Various thin-film deposition techniques such as sputtering and plasma-enhanced chemical vapor deposition (PECVD), employing a capacitively-coupled plasma source, are being investigated for the fabrication of stable and reliable nanocrystalline Si thin films, which are also referred to herein as nanocrystalline Si embedded insulating thin films.

However, conventional PECVD and sputtering techniques have the limitations of low plasma density, inefficient power coupling to the plasma, low ion/neutral ratio, and uncontrolled bulk, and interface damage due to high ion bombardment energy. Therefore, the oxide films formed from a conventional capacitively-coupled plasma (CCP) generated plasma may create reliability issues due to the high bombardment energy of the impinging ionic species. It is important to control or minimize any plasma-induced bulk or interface damage. However, it is not possible to efficiently control the ion energy using the radio frequency (RF) power of CCP generated plasma. Any attempt to enhance the reaction kinetics by increasing the applied power results in increased bombardment of the deposited film, creating a poor quality films with a high defect concentration. Additionally, the low plasma density associated with these types of sources (˜1×10⁸-10⁹ cm⁻³) leads to limited reaction possibilities in the plasma and on the film surface, inefficient generation of active radicals and ions for enhanced process kinetics, inefficient oxidation, and process and system induced impurities, which limits their usefulness in the fabrication of low-temperature electronic devices.

The pulsed laser and ion implantation of Si in dielectric thin films has also been extensively investigated for the creation of Si nano-particles. However, the ion implantation approach is not suitable for the uniform distribution of the nc-Si particles across the film thickness. Additionally, the particle agglomeration in Si ion implanted and pulsed laser deposited dielectric films typically leads to red shift of the PL/EL spectrum.

A deposition process that offers a more extended processing range and enhanced plasma characteristics than conventional plasma-based techniques, such as sputtering or PECVD, is required to generate and control the particle size for PL and electroluminescent (EL) based device development. A process that can enhance plasma density and minimize plasma bombardment will ensure the growth of high quality films without plasma-induced microstructural damage. A process that can offer the possibility of controlling the interface and bulk quality of the films independently will enable the fabrication of high performance and high reliability electronic devices. A plasma process that can efficiently generate the active plasma species, radicals and ions, will enable noble thin film development with controlled process and property control.

For the fabrication of high quality SiOx thin films, the oxidation of a grown film is also critical to ensure high quality insulating layer across the nanocrystalline Si particles. A process that can generate active oxygen radicals at high concentrations will ensure the effective passivation of the Si nanoparticles (nc-Si) in the surrounding oxide matrix. A plasma process that can minimize plasma-induced damage will enable the formation of a high quality interface that is critical for the fabrication of high quality devices. Low thermal budget efficient oxidation and hydrogenation processes are critical and will be significant for the processing of high quality optoelectronic devices. The higher temperature thermal processes can interfere with the other device layers and they are not suitable in terms of efficiency and thermal budget, due to the lower reactivity of the thermally activated species. Additionally, a plasma process which can provide a more complete solution and capability in terms of growth/deposition of novel film structures, oxidation, hydrogenation, particle size creation and control, and independent control of plasma density and ion energy, and large area processing is desired for the development of high performance optoelectronic devices. Also, it is important to correlate the plasma process with the thin film properties as the various plasma parameters dictate the thin film properties and the desired film quality depends on the target application. Some of the key plasma and thin-film characteristics that depend on the target application are deposition rate, substrate temperature, thermal budget, density, microstructure, interface quality, impurities, plasma-induced damage, state of the plasma generated active species (radicals/ions), plasma potential, process and system scaling, and electrical quality and reliability. A correlation among these parameters is critical to evaluate the film quality as the process map will dictate the film quality for the target application. It may not be possible to learn or develop thin-films by just extending the processes developed in low density plasma or other high-density plasma systems, as the plasma energy, composition (radical to ions), plasma potential, electron temperature, and thermal conditions correlate differently depending on the process map.

Si nanocrystals with sizes in the range of 1-10 nm have shown enhanced optical and electrical properties due to quantum confinement effects. One challenge in the development of high performance nc-Si embedded thin film based EL devices are the creation and control of the nc-Si particles sizes and distribution, the properties of the inter-particle medium, and the nc-Si particle/dielectric interface quality. EL device efficiency strongly depends on the intrinsic light generation efficiency of the thin film medium, light extraction efficiency, electrical conductivity, and the breakdown field strength of the film. An efficient charge injection at low applied voltages is a factor in fabricating practical EL devices. Generally, it is possible to get higher EL power from nano-particle embedded films by increasing the film thickness. However, the applied voltage to achieve the target EL power also increases. If the film thickness is reduced to attain the same field at lower voltages, then the EL power level decreases due to the lower number of nano-particles available for light generation.

Low temperatures are generally desirable in liquid crystal display (LCD) manufacture, where large-scale devices are formed on transparent glass, quartz, or plastic substrate. These transparent substrates can be damaged when exposed to temperatures exceeding 650 degrees C. To address this temperature issue, low-temperature Si oxidation processes have been developed. These processes use a high-density plasma source such as an inductively coupled plasma (ICP) source, and are able to form Si oxide with a quality comparable to 1200 degree C. thermal oxidation methods.

The HDP process described herein overcomes the limitations/issues of the deposition rate, film density, nc-Si particle density and size control, bulk and interfacial defect control, defect passivation, and inter-particle medium quality control, when contrasted to the Si ion implantation approach and various physical and chemical techniques currently being investigated for the fabrication of nc-Si embedded dielectric thin films.

It would be advantageous if the benefits realized with high-density plasma deposition could be used in the fabrication of EL devices made from semiconductor nanoparticle embedded Si insulating films. As used herein, a Si insulating film is an insulating film with Si as one of the constituent elements.

SUMMARY OF THE INVENTION

The present invention describes a high-density plasma (HDP) based process for the fabrication of an efficient EL device employing nc-Si embedded SiO_(x)N_(y) thin films with controlled microstructural, optical, and electrical properties. The HDP processed films show high electrical conductivity at low drive voltages, which is critical for efficient light generation by charge carrier induced optical excitations. HDP characteristics have been exploited for the creation of Si nanocrystals in a SiO_(x)N_(y) matrix, with PL emission in the wavelength range of 475-900 nm. The HDP deposited SiO_(x)N_(y) films show PL signal even in the as-deposited state, while a subsequent annealing results in significant enhancement of the PL/EL intensity due to phase separation and quantum confinement effects. It has been found that the nanocrystal size, concentration, and distribution in the as-deposited films are influential in the emission and electrical characteristics of the post-annealed films. The HDP process may be used for the fabrication of single layer, bilayer, or multilayer structures suitable for optoelectronic applications by sequential processing, either in-situ or using a cluster tool. The present invention EL device exhibits a high conductivity at low drive voltages, with free-space EL power far exceeding the nanowatt (nW) level, even at a measurement distance of 20 millimeters (mm) from the top electrode when using an 11.9 mm diameter detector.

Accordingly, a method is provided for fabricating a semiconductor nanoparticle embedded Si insulating film for EL applications. The method provides a bottom electrode, and deposits a semiconductor nanoparticle embedded Si insulating film, including an element selected from a group consisting of N and C, overlying the bottom electrode. After annealing a semiconductor nanoparticle embedded Si insulating film is formed having an extinction coefficient (k) in a range of 0.01-1.0, as measured at about 632 nanometers (nm), and a current density (J) of greater than 1 Ampere per square centimeter (A/cm²) at an applied electric field lower than 3 MV/cm. In another aspect, the annealed semiconductor nanoparticle embedded Si insulating film has an index of refraction (n) in a range of 1.8-3.0, as measured at 632 nm, with a current density of greater than 1 A/cm² at an applied electric field lower than 3 MV/cm.

In one aspect, the semiconductor nanoparticle embedded Si insulating film is deposited by introducing a semiconductor precursor and hydrogen, and using a high density (HD) plasma-enhanced chemical vapor deposition (PECVD) process that supplies power to a top electrode at a frequency in the range of 13.56 to 300 megahertz (MHz), and a power density of less than 5 watts per square centimeter (W/cm²).

Additional details of the above-described method and an EL device with a semiconductor nanoparticle embedded Si insulating film are presented below.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a partial cross-sectional view of an electroluminescence (EL) device with a semiconductor nanoparticle embedded Si insulating film.

FIG. 2 is a graph depicting the relationship between photoluminescence (PL) wavelength and silicon nanoparticle size.

FIG. 3 is a partial cross-sectional view of an EL device with a single layer of silicon nanoparticle embedded SiO_(x)N_(y) film.

FIG. 4 is a partial cross-sectional view of an EL device with multiple layers of silicon nanoparticle embedded SiO_(x)N_(y) film.

FIG. 5 is a partial cross-sectional view of an EL device with multiple layers of silicon nanoparticle embedded SiO_(x)N_(y) film, and additional optical layers.

FIG. 6 is a schematic drawing of a high-density plasma (HDP) system with an inductively coupled plasma source.

FIG. 7 is a graph depicting effect of RF power on charge trapping characteristics.

FIGS. 8A and 8B depict the effect of the RF power on leakage current and EL power, respectively.

FIG. 9A is a graph depicting the relationship between EL power and applied voltage for nc-Si embedded SiOxNy thin films deposited on various substrates.

FIG. 9B is a graph depicting the relationship between current density and EL power, at k=0.0392.

FIGS. 10A and 10B depict the effect of the annealing temperature on the PL response (FIG. 10A) and the PL spectra of the films as a function of the rapid thermal annealing temperature (FIG. 10B).

FIG. 11 is a graph depicting PL emission characteristics of films deposited using a combination of SiH₄/N₂O/Kr/H₂.

FIG. 12 depicts the effect of hydrogen defect passivation on the PL response of a film with a peak emission wavelength of about 880 nm.

FIGS. 13A and 13B are a flowchart illustrating a method for fabricating a semiconductor nanoparticle embedded Si insulating film for EL applications.

DETAILED DESCRIPTION

FIG. 1 is a partial cross-sectional view of an electroluminescence (EL) device with a semiconductor nanoparticle embedded Si insulating film. The EL device 100 comprises a bottom electrode 102. The bottom electrode 102 may be a doped semiconductor, metal, or polymer. A semiconductor nanoparticle embedded Si insulating film 104 overlies the bottom electrode 102. The semiconductor nanoparticle embedded Si insulating film 104 includes either the element of N or C, and has an extinction coefficient (k) in a range of 0.01-1.0, as measured at about 632 nanometers (nm). Simultaneously, the semiconductor nanoparticle embedded Si insulating film 104 has a current density (J) of greater than 1 Ampere per square centimeter (A/cm²) at an applied electric field lower than 3 MV/cm.

The semiconductor nanoparticles embedded in the Si insulating film 104 have a diameter in the range of about 1 to 10 nanometers (nm), and are made from either Si or Ge. A top electrode 106 overlies the semiconductor nanoparticle embedded Si insulating film 104. The top electrode may be a thin metal or transparent metal oxide such as indium tin oxide (ITO), for example.

It has been possible to fabricate high performance nc-Si embedded dielectric films by analyzing the key high density plasma process parameters impacting the optical dispersion, nc-Si growth, and size as evidenced in the PL response of the films. The n-k dispersion can be controlled by varying the N/O ratio, as well as the Si richness in the films. The PL response characteristics can be addressed by controlling the nc-Si size, which strongly depends on the system pressure and RF power. However, the correlation among these thin film properties and high density plasma deposition conditions needed to fabricate high performance EL devices operating at low voltages has been, before now, impossible to determine due to the large number of variables.

Simultaneous with the current density being greater than 1 A/cm² at an applied electric field lower than 3 MV/cm, the semiconductor nanoparticle embedded Si insulating film 104 has an index of refraction (n) in a range of 1.8-3.0, as measured at 632 nm.

More explicitly, the semiconductor nanoparticle embedded Si insulating film 104 may be a non-stoichiometric SiO_(X)N_(Y) thin-film, where (X+Y<2 and Y>0), or SiC_(X), where X<1. In one aspect, the semiconductor nanoparticle embedded Si insulating film 104 exhibits a spectral response at a wavelength in the range of about 200 nm to about 1600 nm. In another aspect, the semiconductor nanoparticle embedded Si insulating film 104 includes a Type 3, Type 4, Type 5, or rare earth elements dopant, and the EL device 100 has optical absorption characteristics in the range of frequencies from deep ultraviolet (UV) to far infrared (IR).

FIG. 2 is a graph depicting the relationship between photoluminescence (PL) wavelength and silicon nanoparticle size. The development of nc-Si embedded Si thin films with PL emissions covering the visible part of the spectrum is attractive for diverse opto-electronic applications. The high-density plasma (HDP) process described below is effective in the creation and control of the nc-Si particles in the range of 1-10 nm.

Some factors that strongly influence optical quantum efficiency and EL device performance are summarized in Table 1. The deposition technique, post-deposition annealing conditions, defect passivation efficiency, and film/electrode interface all play a role in dictating the overall performance of the PL/EL devices.

TABLE 1 Factors influencing the performance of EL devices employing nc-Si embedded dielectric thin films Factors Influencing EL Performance nc-Si size and density distribution Inter-particle dielectric material Dielectric medium quality nc-Si/dielectric interface quality non-radiative defect centers and their passivation Optical dispersion characteristics Charge injection efficiency at the interface and in the bulk of the film

FIG. 3 is a partial cross-sectional view of an EL device with a single layer of silicon nanoparticle embedded SiO_(x)N_(y) film. The nc-Si thin film has a current density exceeding 1 A/cm². The hole and electron injecting layers can be a single or multilayer structures to enhance the carrier injection into the nc-Si embedded dielectric film. The spectral response and the electrical conductivity of the nc-Si thin film can be further modified by in-situ or ex-situ doping by any suitable method.

FIG. 4 is a partial cross-sectional view of an EL device with multiple layers of silicon nanoparticle embedded SiO_(x)N_(y) film. At least one layer has high electrical conductivity, while other layers incorporate nc-Si particles of different sizes for spectral tuning.

FIG. 5 is a partial cross-sectional view of an EL device with multiple layers of silicon nanoparticle embedded SiO_(x)N_(y) film, and additional optical layers. The multilayer EL device can incorporate various optical layers for light emission by electrical and/or optical excitations in the visible to IR wavelength range. Some examples of optical layers include quantum dots (QDs) in a dielectric or semiconducting medium, wide bandgap semiconductors, polymers, and dielectrics.

The high-density PECVD (HDPECVD) process is effective in the low temperature processing of Si nanocrystal films having good PL characteristics, even in the as-deposited state. The HDP technique is attractive for processing high quality Si (amorphous, microcrystalline, polycrystalline, or nanocrystalline), SiO₂, SiN_(x), and stoichiometric and Si rich SiO_(x)N_(y) thin films for the fabrication of stable and reliable optoelectronic devices. The HDP-based processes enable the fabrication of high-quality single and multi-layer superlattice structures suitable for the fabrication of efficient and reliable optoelectronic devices. The fabrication of electroluminescent devices based on the photo-emission characteristics of nanocrystalline Si will dictate the development of high performance and cost-effective integrated optoelectronic devices. Another application of the SiO_(x)N_(y) thin films is in flash memory. The nc-Si embedded dielectric films can serve the dual purposes of charge trapping and light emission.

FIG. 6 is a schematic drawing of a high-density plasma (HDP) system with an inductively coupled plasma source. The top electrode 1 is driven by a high frequency radio frequency (RF) source 2, while the bottom electrode 3 is driven by a lower frequency power source 4. The RF power is coupled to the top electrode 1, from the high-density inductively coupled plasma (ICP) source 2, through a matching network 5 and high pass filter 7. The power to the bottom electrode 3, through a low pass filter 9 and matching transformer 11, can be varied independently of the top electrode 1. The top electrode power frequency can be in the range of about 13.56 to about 300 megahertz (MHz) depending on the ICP design. The bottom electrode power frequency can be varied in the range of about 50 kilohertz (KHz) to about 13.56 MHz, to control the ion energy. The pressure can be varied up to 500 mTorr. The top electrode power can be as great as about 10 watts per square-centimeter (W/cm²), although the above-described semiconductor nanocrystal embedded Si insulating films are typically formed using a top electrode power of less than 5 W/cm². The bottom electrode power can be as great as about 3 W/cm².

One interesting feature of the HDP system is that there are no inductive coils exposed to the plasma, which eliminates any source-induced impurities. The power to the top and bottom electrodes can be controlled independently. There is no need to adjust the system body potential using a variable capacitor, as the electrodes are not exposed to the plasma. That is, there is no crosstalk between the top and bottom electrode powers, and the plasma potential is low, typically less than 20 V. System body potential is a floating type of potential, dependent on the system design and the nature of the power coupling.

The HDP tool is a true high-density plasma process with an electron concentration of greater than 1×10¹¹ cm⁻³, and the electron temperature is less than 10 eV. There is no need to maintain a bias differential between the capacitor connected to the top electrode and the system body, as in many high-density plasma systems and conventional designs such as capacitively-coupled plasma tools. Alternately stated, both the top and bottom electrodes receive RF and low frequency (LF) powers.

Process parameters and nc-Si embedded SiO_(x)N_(y) thin film characteristics suitable for the fabrication of high performance EL devices are listed in Table 2. The HDP process is effective in controlling the optical dispersion, PL, electrical, and EL characteristics of nc-Si embedded SiO_(x)N_(y) thin films over a wide range.

TABLE 2 Process parameters and thin-film characteristics for the fabrication of efficient EL devices Parameter Range Process Gas H₂ RF Power Density <5 W/cm² Refractive Index (n) 1.8-3.0 @ 632 nm Electrical Conductivity J > 1 A/cm² @E < 3 MV/cm

The creation and control of the nc-Si particle size, density, and distribution is a factor in the fabrication of high performance optoelectronic devices. H₂ gas in the plasma is very effective in controlling the nc-Si size and optical dispersion characteristics. The combination of the various processes described herein is effective in the creation of nc-Si particles exhibiting PL response in the wavelength range of 475-900 nm. SiO_(x)N_(y) thin film properties are controlled by varying the gas flow rate and ratios, RF power, system pressure, and substrate temperature. The deposition process is optimized in terms of the optical, PL, and EL emission characteristics of the SiO_(x)N_(y) thin films. The various gas combinations and the flow ratios, which are effective in the fabrication of high quality nc-Si embedded SiO_(x)N_(y) thin-films, are described in Table 3.

TABLE 3 Gas combinations and flow ratios suitable for the fabrication of nc-Si embedded SiO_(x)N_(y) thin films for PL/EL applications Gas Combination Examples Comment Source of Si Silane Family Required for Si Source of N₂O, O₂, etc Required for Oxygen oxygen Hydrogen H₂ Critical for High conductivity and nc-Si size control. H₂ Flow H₂/(total flow of >2 times the flow of other gases other gases) Other Gases Noble gases, N₂, Can be added for further control of etc. nc-Si size/density/distribution and dielectric medium microstructure and property

Details of HDP process conditions for the fabrication of stoichiometric and Si rich SiO_(x)N_(y) thin films are detailed in Table 4.

TABLE 4 High density plasma processing of SiO_(x)N_(y) thin films Top Electrode Power 13.56-300 MHz, <5 W/cm², Bottom Electrode 50 KHz-13.56 MHz, <3 W/cm² Power Pressure 1-500 mTorr Temperature 25-300° C. Film Thickness (nm) 5 nm-1 μm

FIG. 7 is a graph depicting effect of RF power on charge trapping characteristics. RF power has a strong influence on the charge trapping characteristics of the nc-Si embedded dielectric film. The charge trapping in turn depends on the nc-Si particle density in the dielectric matrix. FIG. 7 shows the effect of RF power on capacitance-voltage (C-V) voltage hysteresis in 100 nm-thick films. Lower RF power levels enhance the Si richness in the film, which in turn leads to higher conductivity and enhanced charge trapping. The higher electrical conductivity is useful in the fabrication of high performance EL devices operating at low voltages.

FIGS. 8A and 8B depict the effect of the RF power on leakage current and EL power, respectively. As shown, leakage current density and EL response both improve significantly with decreasing RF power. Typically, power levels below 500 W are required for the high conductivity thin films exhibiting EL power far exceeding the nW level.

FIG. 9A is a graph depicting the relationship between EL power and applied voltage for nc-Si embedded SiOxNy thin films deposited on various substrates. The EL response of nc-Si embedded SiO_(x)N_(y) thin films is strongly dependent upon conductivity and the type of dopant in the substrate. The measured EL response is only a lower limit of the true capability of the nc-Si embedded SiO_(x)N_(y) thin films. The EL response can be further influenced by doping the films to control the electrical characteristics and the spectral response. Additionally, several extrinsic factors such as electrode material, nature of majority carriers, multilayer electrode structures for injection barrier control, etc, can be tailored for optimum EL response for the target application.

FIG. 9B is a graph depicting the relationship between current density and EL power, at k=0.0392. As shown, the current density (J)>1 A/cm² at E<3 MV/cm, with k (at 632 nm)=0.0392, corresponds to an EL power>1 nW.

Table 5 shows the effect of H₂ flow on the refractive index of the SiO_(x)N_(y) thin films deposited at an RF power of 1500 W and system pressure of 75 mTorr. The refractive index increases with an increase in the hydrogen flow, leading to an increased nc-Si particle size, which indicates an increase in the Si richness of the films. Similar relationships are observed in the processes listed in Tables 3 and 4.

TABLE 5 Effect of H₂ flow on the refractive index of SiO_(x)N_(y) thin films SiH₄ (sccm) N₂O (sccm) H₂ (sccm) n @ 632 nm 5 5 250 1.774 5 5 325 1.793 5 5 400 1.817 5 5 475 1.852

FIGS. 10A and 10B depict the effect of the annealing temperature on the PL response (FIG. 10A) and the PL spectra of the films as a function of the rapid thermal annealing temperature (FIG. 10B). The films were deposited at a SiH₄/N₂O/H₂ ratio of 15/15/150 sccm. The applied RF power, system pressure, and substrate temperature were 700 W, 75 mTorr, and 270° C., respectively. As shown in FIG. 10A, the PL emission wavelength is maintained at around 500 nm for the as-deposited and annealed films. FIG. 10B shows a well defined PL peak at 500 nm.

FIG. 11 is a graph depicting PL emission characteristics of films deposited using a combination of SiH₄/N₂O/Kr/H₂. The combination of the inert gas and hydrogen are very effective in the creation of larger nc-Si particles; especially, ones exhibiting PL response in the range of 800-900 nm.

FIG. 12 depicts the effect of hydrogen defect passivation on the PL response of a film with a peak emission wavelength of about 880 nm. A high-density plasma hydrogenation process is attractive for an efficient low temperature and low thermal budget passivation of defects and dangling bonds in the deposited Si, SiO_(x)N_(y) and SiO₂ thin films. Table 6 summarizes the high-density plasma processing conditions suitable for the efficient hydrogenation of thin films.

TABLE 6 High density plasma hydrogenation process range Top Electrode Power 13.56-300 MHz, up to 10 W/cm², Bottom Electrode 50 KHz-13.56 MHz, up to 3 Power W/cm² Pressure 1-500 mTorr Gases: General H₂ + Any suitable Inert Gas Gases: Specific Process H₂ Temperature 25-300° C. Time 30 s-60 min

The presence of an appreciable. PL/EL signal in the as-deposited thin film shows the potential of the HDP process in creating Si nanocrystals, even at temperatures lower than 300° C. The PL/EL emission characteristics of the SiO_(x)N_(y) thin films can be further enhanced by thermal treatment in a suitable ambient. The high-temperature annealing results in a separation of the SiO_(x)N_(y) phase into Si clusters or nanocrystals separated by a dielectric matrix. The annealing temperature/time can be correlated with other thin-film deposition process conditions and properties so that the Si cluster size, concentration, and distribution can be varied. Exemplary annealing conditions are listed in Table 7.

TABLE 7 Post-deposition thermal annealing range for nc-Si embedded SiO_(x)N_(y) thin films. Temperature Range 300-1100° C. Time 10-60 min Ambient Inert gas/H₂

As used herein, a nc-Si embedded SiO_(x)N_(y) (x+y<2) thin film is also referred to as a non-stoichiometric SiO_(X)N_(Y) thin-film, where (X+Y<2 and Y>0). A non-stoichiometric SiO_(X)N_(Y) thin-film, as used herein, is understood to be a film with Si nanoparticles (nc-Si), and may also be referred to as a Si-rich SiO_(X)N_(Y) thin-film. The term “non-stoichiometric” as used herein retains the meaning conventionally understood in the art as a chemical compound with an elemental composition that cannot be represented by a ratio of well-defined natural numbers and is, therefore, in violation of the law of definite proportions. Conventionally, a non-stoichiometric compound is a solid that is understood to include random defects, resulting in the deficiency of one element. Since the compound needs to be overall electrically neutral, the missing atom's charge requires compensation in the charge for another atom in the compound, by either changing the oxidation state, or by replacing it with an atom of a different element with a different charge. More particularly, the “defect” in a non-stoichiometric SiO_(X)N_(Y) involves nanocrystalline particles.

FIGS. 13A and 13B are a flowchart illustrating a method for fabricating a semiconductor nanoparticle embedded Si insulating film for EL applications. Although the method is depicted as a sequence of numbered steps for clarity, the numbering does not necessarily dictate the order of the steps. It should be understood that some of these steps may be skipped, performed in parallel, or performed without the requirement of maintaining a strict order of sequence. The method starts at Step 1300.

Step 1302 provides a bottom electrode. Step 1304 deposits a semiconductor nanoparticle embedded Si insulating film including either the element N or C, overlying the bottom electrode. For example, the semiconductor nanoparticle embedded Si insulating film may be non-stoichiometric SiO_(X)N_(Y) thin-film, where (X+Y<2 and Y>0). The optical dispersion characteristics of the non-stoichiometric SiO_(X)N_(Y) thin-film films can also be tailored by varying the values of X and Y with respect to the thickness of the thin-film. Alternately, the semiconductor nanoparticle embedded Si insulating film may be SiC_(X), where X<1. The semiconductor nanoparticles are either Si or Ge. In one aspect, the semiconductor thin-film is deposited by heating an underlying substrate to a temperature of less than about 400° C. Note: in some aspects the bottom electrode and substrate are the same element.

Step 1306 anneals the semiconductor nanoparticle embedded Si insulating film. Step 1308 forms an annealed semiconductor nanoparticle embedded Si insulating film having an extinction coefficient (k) in a range of 0.01-1.0, as measured at about 632 nanometers (nm), and a current density (J) of greater than 1 Ampere per square centimeter (A/cm²) at an applied electric field lower than 3 MV/cm. Alternately, Step 1308 forms an annealed semiconductor nanoparticle embedded Si insulating film having an index of refraction (n) in a range of 1.8-3.0, as measured at 632 nm, with the current density of greater than 1 A/cm² at an applied electric field lower than 3 MV/cm. In Step 1310 the annealed semiconductor nanoparticle embedded Si insulating film exhibits a spectral response at a wavelength in a range of about 200 nm to about 1600 nm.

In one aspect, depositing the semiconductor nanoparticle embedded Si insulating film in Step 1304 includes substeps. Step 1304 a introduces a semiconductor precursor and hydrogen. Step 1304 b deposits a semiconductor thin-film overlying the bottom electrode, using a HDPECVD process. Step 1304 c supplies power to a top electrode at a frequency in the range of 13.56 to 300 megahertz (MHz), and a power density of less than 5 watts per square centimeter (W/cm²). Step 1304 d supplies power to a bottom electrode at a frequency in the range of 50 kilohertz to 13.56 MHz, and a power density of up to 3 W/cm². In one aspect, Step 1304 a uses an atmosphere pressure in the range of 1 to 500 mTorr, and supplies an oxygen source gas. For example, N₂O, NO, O₂, or O₃ may be used. In another aspect, Step 1304 a supplies an inert noble gas in addition to the oxygen source gas. In a different aspect, Step 1304 a introduces the semiconductor precursor and hydrogen with a nitrogen source gas, such as N₂ or NH₃.

In one aspect, the HDPECVD process uses an inductively coupled plasma (ICP) source. In another aspect, the HDPECVD process uses a plasma concentration of greater than 1×10¹¹ cm⁻³, with an electron temperature of less than 10 eV. It should be noted that the semiconductor nanoparticle embedded Si insulating films may be fabricated by any suitable high density plasma technique operating at RF or microwave frequencies.

In another aspect, supplying the semiconductor precursor and hydrogen in Step 1304 a includes supplying a precursor such as Si_(n)H_(2n+2) or Ge_(n)H₂₊₂, where n varies from 1 to 4, SiH_(x)R_(4−x) where R is Cl, Br, or I, and where x varies from 0 to 3, or GeH_(x)R_(4−x) where R is Cl, Br, or I, and x varies from 0 to 3. In this manner, SiO_(X)N_(Y) thin-film is formed. Alternately, if Step 1304 deposits a SiC_(X) thin-film, the C source may be any suitable hydrocarbon-containing precursor. Some examples of hydrocarbon-containing precursors include alkanes (C_(n)H_(2n+2)), alkenes (C_(n)H_(2n)), alkynes (C_(n)H_(2n−2)), Benzene (C₆H₆), and Toluene (C₇H₈).

The annealed semiconductor nanoparticle embedded Si insulating film formed in Step 1308 may be an intrinsic or doped semiconductor nanoparticle embedded Si insulating films. If doped, the dopant may be a Type 3, Type 4, Type 5, or rare earth element dopant. Then, in Step 1312, the annealed semiconductor nanoparticle embedded Si insulating film exhibits optical absorption characteristics in the range of frequencies from deep ultraviolet (UV) to far infrared (IR).

In another aspect, annealing the semiconductor nanoparticle embedded Si insulating film in Step 1306 includes using either a flash or laser annealing, with a heat source having a radiation wavelength of either about 150 to 600 nm or about 9 to 11 micrometers. In a different aspect, annealing the semiconductor nanoparticle embedded Si insulating film includes substeps. Step 1306 a heats the substrate to a temperature of greater than about 400° C. Step 1306 b heats for a time duration in the range of about 10 to 300 minutes. Step 1306 c heats in an atmosphere of oxygen and hydrogen, oxygen, hydrogen, or inert gases. Then, forming the annealed semiconductor nanoparticle embedded Si insulating film in Step 1308 includes modifying the size of the semiconductor nanoparticles in the Si insulating film in response to the annealing.

In another aspect, if Step 1302 provides a bottom electrode on a temperature-sensitive substrate such as glass, a metalized substrate, or plastic, then Step 1306 may anneal the semiconductor nanoparticle embedded Si insulating film at a temperature of less than 650° C.

In a different aspect, Step 1309 a performs a HD plasma treatment on the annealed semiconductor nanoparticle embedded Si insulating film in an H₂ atmosphere, using a substrate temperature of less than 400° C. Step 1309 b hydrogenates the annealed semiconductor nanoparticle embedded Si insulating film. For example, the hydrogenating may be accomplished using an HD plasma process as follows:

supplying power to a top electrode at a frequency in the range of 13.56 to 300 MHz, and a power density of up to 10 W/cm²;

supplying power to a bottom electrode at a frequency in the range of 50 kilohertz to 13.56 MHz, and a power density of up to 3 W/cm²;

using an atmosphere pressure in the range of 1 to 500 mTorr; and,

supplying an atmosphere or either H₂ and an inert gas, or H₂.

EL devices have been described that are made with semiconductor nanoparticles embedded Si insulating films. Specific examples of SiO_(X)N_(Y) thin-films and SiC_(X) thin-film fabrication details have been presented. Some details of other specific materials and process details have also been used to illustrate the invention. However, the invention is not limited to merely these examples. Other variations and embodiments of the invention will occur to those skilled in the art. 

1. A method for fabricating a semiconductor nanoparticle embedded Si insulating film for electroluminescence (EL) applications, the method comprising: providing a bottom electrode; depositing a semiconductor nanoparticle embedded Si insulating film including an element selected from a group consisting of N and C, overlying the bottom electrode; annealing the semiconductor nanoparticle embedded Si insulating film; and, forming an annealed semiconductor nanoparticle embedded Si insulating film having an extinction coefficient (k) in a range of 0.01-1.0, as measured at about 632 nanometers (nm), and a current density (J) of greater than 1 Ampere per square centimeter (A/cm²) at an applied electric field lower than 3 MV/cm.
 2. The method of claim 1 wherein depositing the semiconductor nanoparticle embedded Si insulating film includes: introducing a semiconductor precursor and hydrogen; depositing a semiconductor thin-film overlying the bottom electrode, using a high density (HD) plasma-enhanced chemical vapor deposition (PECVD) process; and, supplying power to a top electrode at a frequency in the range of 13.56 to 300 megahertz (MHz), and a power density of less than 5 watts per square centimeter (W/cm²).
 3. The method of claim 2 further comprising: supplying power to a bottom electrode at a frequency in the range of 50 kilohertz to 13.56 MHz, and a power density of up to 3 W/cm²; wherein introducing the semiconductor precursor and hydrogen includes: using an atmosphere pressure in the range of 1 to 500 mTorr; and, supplying an oxygen source gas.
 4. The method of claim 3 wherein supplying the oxygen source gas includes supplying an oxygen source gas selected from a group consisting of N₂O, NO, O₂, and O₃.
 5. The method of claim 3 wherein introducing the semiconductor precursor and hydrogen includes supplying an inert noble gas.
 6. The method of claim 3 wherein introducing the semiconductor precursor and hydrogen includes supplying a nitrogen source gas, selected from a group consisting of N₂ and NH₃.
 7. The method of claim 1 wherein annealing the semiconductor nanoparticle embedded Si insulating film includes using an annealing process selected from a group consisting of flash and laser annealing, using a heat source having a radiation wavelength selected from a group consisting of about 150 to 600 nm and 9 to 11 micrometers.
 8. The method of claim 2 wherein depositing the semiconductor thin-film using the HD PECVD process includes using a plasma concentration of greater than 1×10¹¹ cm⁻³, with an electron temperature of less than 10 eV.
 9. The method of claim 1 wherein depositing the semiconductor nanoparticle embedded Si insulating film includes depositing semiconductor nanoparticles selected from a group consisting of Si and Ge.
 10. The method of claim 2 wherein introducing the semiconductor precursor and hydrogen includes supplying a precursor selected from a group consisting of Si_(n)H_(2n+2) and Ge_(n)H_(2n+2), where n varies from 1 to 4, SiH_(x)R_(4−x) where R is selected from a first group consisting of Cl, Br, and I, and where x varies from 0 to 3, and GeH_(x)R_(4−x) where R is selected from the first group, and x varies from 0 to
 3. 11. The method of claim 2 wherein depositing the semiconductor thin-film using an HD PECVD process includes using an inductively coupled plasma (ICP) source.
 12. The method of claim 1 wherein forming the annealed semiconductor nanoparticle embedded Si insulating film includes forming a film selected from a group consisting of a non-stoichiometric SiO_(X)N_(Y) thin-film, where (X+Y<2 and Y>0), and SiC_(X), where X<1.
 13. The method of claim 1 further comprising: the annealed semiconductor nanoparticle embedded Si insulating film exhibiting a spectral response at a wavelength in a range of about 200 nm to about 1600 nm.
 14. The method of claim 2 wherein depositing the semiconductor thin-film includes heating an underlying substrate to a temperature of less than about 400° C.
 15. The method of claim 1 wherein annealing the semiconductor nanoparticle embedded Si insulating film includes: heating an underlying substrate to a temperature of greater than about 400° C.; heating for a time duration in the range of about 10 to 300 minutes; heating in an atmosphere selected from a group consisting of oxygen and hydrogen, oxygen, hydrogen, and inert gases; and, wherein forming the annealed semiconductor nanoparticle embedded Si insulating film includes modifying the size of the semiconductor nanoparticles in the Si insulating film in response to the annealing.
 16. The method of claim 1 wherein providing a bottom electrode includes providing a bottom electrode on a temperature-sensitive substrate selected from a group consisting of glass, metalized substrates, and plastic; wherein annealing the semiconductor nanoparticle embedded Si insulating film includes annealing at a temperature of less than 650° C.
 17. The method of claim 1 wherein forming an annealed semiconductor nanoparticle embedded Si insulating film includes forming an annealed semiconductor nanoparticle embedded Si insulating film selected from a group consisting of intrinsic and doped semiconductor nanoparticle embedded Si insulating films.
 18. The method of claim 17 wherein forming an annealed semiconductor nanoparticle embedded Si insulating film with dopant includes: forming an annealed semiconductor nanoparticle embedded Si insulating film with a dopant selected from a group consisting of Type 3, Type 4, Type 5, and rare earth, elements; and, in response to doping, forming an annealed semiconductor nanoparticle embedded Si insulating film exhibiting optical absorption characteristics in a range of frequencies from deep ultraviolet (UV) to far infrared (IR).
 19. The method of claim 1 wherein forming an annealed semiconductor nanoparticle embedded Si insulating film includes forming an annealed semiconductor nanoparticle embedded Si insulating film having an index of refraction (n) in a range of 1.8-3.0, as measured at 632 nm, with a current density of greater than 1 A/cm² at an applied electric field lower than 3 MV/cm.
 20. The method of claim 1 further comprising: performing a HD plasma treatment on the annealed semiconductor nanoparticle embedded Si insulating film in an H₂ atmosphere, using a substrate temperature of less than 400° C.; and, hydrogenating the annealed semiconductor nanoparticle embedded Si insulating film.
 21. The method of claim 20 wherein hydrogenating the annealed semiconductor nanoparticle embedded Si insulating film using the HD plasma process includes: supplying power to a top electrode at a frequency in the range of 13.56 to 300 MHz, and a power density of up to 10 W/cm²; supplying power to a bottom electrode at a frequency in the range of 50 kilohertz to 13.56 MHz, and a power density of up to 3 W/cm²; using an atmosphere pressure in the range of 1 to 500 mTorr; and, supplying an atmosphere selected from a group consisting of H₂ and an inert gas, and H₂. 